WO2021112519A1 - 굽힘 가공성 및 내식성이 우수한 용융아연도금강판 및 이의 제조방법 - Google Patents

굽힘 가공성 및 내식성이 우수한 용융아연도금강판 및 이의 제조방법 Download PDF

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WO2021112519A1
WO2021112519A1 PCT/KR2020/017344 KR2020017344W WO2021112519A1 WO 2021112519 A1 WO2021112519 A1 WO 2021112519A1 KR 2020017344 W KR2020017344 W KR 2020017344W WO 2021112519 A1 WO2021112519 A1 WO 2021112519A1
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Prior art keywords
steel sheet
hot
mgzn
plating
corrosion resistance
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PCT/KR2020/017344
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English (en)
French (fr)
Korean (ko)
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김성주
김흥윤
김명수
강대영
김용주
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주식회사 포스코
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Priority to US17/782,401 priority Critical patent/US20230019786A1/en
Priority to JP2022532730A priority patent/JP2023504496A/ja
Priority to CN202080084257.3A priority patent/CN114787411B/zh
Priority to EP20897267.9A priority patent/EP4071265A4/en
Publication of WO2021112519A1 publication Critical patent/WO2021112519A1/ko

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B32B15/013—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of a metal other than iron or aluminium
    • B—PERFORMING OPERATIONS; TRANSPORTING
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    • B32B15/04—Layered products comprising a layer of metal comprising metal as the main or only constituent of a layer, which is next to another layer of the same or of a different material
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    • B32B15/04—Layered products comprising a layer of metal comprising metal as the main or only constituent of a layer, which is next to another layer of the same or of a different material
    • B32B15/043—Layered products comprising a layer of metal comprising metal as the main or only constituent of a layer, which is next to another layer of the same or of a different material of metal
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    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12861—Group VIII or IB metal-base component
    • Y10T428/12951—Fe-base component
    • Y10T428/12972—Containing 0.01-1.7% carbon [i.e., steel]
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/24—Structurally defined web or sheet [e.g., overall dimension, etc.]
    • Y10T428/24942—Structurally defined web or sheet [e.g., overall dimension, etc.] including components having same physical characteristic in differing degree
    • Y10T428/2495—Thickness [relative or absolute]
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/24—Structurally defined web or sheet [e.g., overall dimension, etc.]
    • Y10T428/24942—Structurally defined web or sheet [e.g., overall dimension, etc.] including components having same physical characteristic in differing degree
    • Y10T428/2495—Thickness [relative or absolute]
    • Y10T428/24967—Absolute thicknesses specified
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/26—Web or sheet containing structurally defined element or component, the element or component having a specified physical dimension
    • Y10T428/263—Coating layer not in excess of 5 mils thick or equivalent
    • Y10T428/264—Up to 3 mils
    • Y10T428/265—1 mil or less
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/27—Web or sheet containing structurally defined element or component, the element or component having a specified weight per unit area [e.g., gms/sq cm, lbs/sq ft, etc.]

Definitions

  • the present invention relates to a hot-dip galvanized steel sheet having excellent bending workability and corrosion resistance and a method for manufacturing the same.
  • the Zn-Mg-Al-based zinc alloy plated steel sheet has excellent corrosion resistance, but has a disadvantage in that the bending workability is poor. That is, the zinc alloy plated steel sheet contains a large amount of Zn-Al-Mg-based intermetallic compounds formed by thermodynamic interaction of Zn, Al and Mg in the plating layer. It causes cracks, which has a disadvantage in that bending workability is deteriorated. Such cracks damage the appearance of the bent portion or cause deterioration of corrosion resistance.
  • the technique of adding a small amount of Si is generally finely controlled to 0.1 to 0.2 wt %, but when it is excessively added, an additional alloy phase in the form of Mg 2 Si may be coarsely formed in the plating layer. Therefore, it can be seen that securing continuous bending workability is a very important characteristic related to stability of molding and corrosion resistance after processing.
  • Patent Document 1 Japanese Patent Laid-Open No. JP2003-155549
  • the present invention is to solve the problems of the prior art, and a hot-dip galvanized steel sheet having a Zn-Al-Mg-based plating layer capable of securing excellent bending workability and corrosion resistance by reducing cracks in the plating layer during bending forming and its To provide a manufacturing method.
  • One aspect of the present invention is
  • An interfacial alloy layer of Fe-Al-Zn composition formed between the base steel sheet and the plating layer,
  • the interfacial alloy layer has a thickness of 0.5 to 2 ⁇ m and has a dendritic form
  • Plated layer of the Zn-Mg-Al-based is Zn-Al-MgZn 2 3 ternary process organization, Zn-MgZn 2 2 alloy process tissue, having a tissue containing Zn is employed with Al at least one of the single-phase tissue and Zn single phase tissue , MgZn 2 It relates to a hot-dip galvanized steel sheet excellent in bending workability and corrosion resistance, characterized in that the aggregated Al is contained in the structure.
  • the Al and Mg content may be determined to be located in the 2 eutectic line of MgZn 2 and Al in the Mg-Al-Zn ternary phase diagram.
  • the width of the bending crack generated during 90 degree bending and 0T bending of the plating layer including the base steel sheet may be 30 ⁇ m or less and 100 ⁇ m or less, respectively.
  • Hot-dip galvanizing the base steel sheet in a plating bath containing, by weight, Al: 5.1 to 25%, Mg: 4.0 to 10%, the remaining Zn and other unavoidable impurities; and
  • the interfacial alloy layer and Zn-Mg- on the base steel sheet by cooling the plated steel sheet using an inert gas at a cooling rate of 5 to 30°C/s from the plating bath surface to the top roll section. Including; manufacturing a hot-dip galvanized steel sheet in which Al-based plating layers are sequentially formed;
  • Plated layer of the Zn-Mg-Al-based is Zn-Al-MgZn 2 3 ternary process organization, Zn-MgZn 2 2 alloy process tissue, having a tissue containing Zn is employed with Al at least one of the single-phase tissue and Zn single phase tissue , MgZn 2 Agglomerated Al may be included in the structure.
  • the temperature of the plating bath can be maintained in the range of 470 ⁇ 520 °C.
  • Al and Mg content in the plating bath may be determined to be located in the MgZn 2 and Al 2 process line of the Mg-Al-Zn ternary phase diagram.
  • the bath time in which the base steel sheet is immersed in the plating bath may be 1 to 5 seconds.
  • the inert gas may be one of N, Ar, and He.
  • the hot-dip galvanized steel sheet according to the present invention has advantages of excellent bending workability and corrosion resistance.
  • the cracks measured by performing a 90 degree bending test on a hot-dip galvanized steel sheet having a plating layer containing no Si, Al: 5.1 to 25% by weight, and Mg: 4.0 to 10% by weight It is possible to provide a hot-dip galvanized steel sheet having an excellent bending workability and excellent corrosion resistance even after processing as the width is as low as 30 ⁇ m or less.
  • Example 1 is a cross-section of the hot-dip galvanized steel sheet of Inventive Example 1, which is a preferred embodiment of the present invention, observed with a Field Emission Scanning Electron Microscope (hereinafter referred to as 'FE-SEM') (magnification ⁇ 2,000 times) it's one picture
  • 'FE-SEM' Field Emission Scanning Electron Microscope
  • FIG. 2 is a photograph of the surface of the interfacial alloy layer of the hot-dip galvanized steel sheet of Invention Example 1, which is a preferred embodiment of the present invention, observed by FE-SEM (magnification ⁇ 10,000 times).
  • Example 5 is a 90 degree bending process of the hot-dip galvanized steel sheet of Inventive Example 1, which is a preferred embodiment of the present invention, and observing cracks generated at the top of the bending process by FE-SEM (magnification ⁇ 100, ⁇ 200, ⁇ 300 times) they are pictures
  • the hot-dip galvanized steel sheet of the present invention is a base steel sheet; It is provided on at least one surface of the base steel sheet, and with respect to the remaining components except for iron (Fe) diffused from the base steel sheet, in weight %, Al: 5.1 to 25%, Mg: 4.0 to 10%, the remaining Zn and other unavoidable a Zn-Mg-Al-based plating layer containing impurities; and an interfacial alloy layer of Fe-Al-Zn composition formed between the base steel sheet and the plating layer.
  • Fe iron
  • the interface between the alloy layer has a dendritic shape and the thickness is 0.5 ⁇ 2 ⁇ m
  • a hot-dip galvanized steel sheet according to an aspect of the present invention, a base steel sheet; a Zn-Mg-Al-based plating layer provided on at least one surface of the base steel sheet; and an Fe-Al-Zn interface alloy layer formed between the base steel sheet and the plating layer.
  • At least one surface of the base steel sheet may be provided with a plating layer made of a Zn-Mg-Al-based alloy.
  • the plating layer may be formed only on one side of the holding steel sheet, it may be formed on both sides of the holding steel sheet.
  • the Zn-Mg-Al-based plating layer is, with respect to the remaining components except for a small amount of iron (Fe) diffused from the base steel sheet, in wt%, Al: 5.1 to 25%, Mg: 4.0 to 10% , remaining Zn and other unavoidable impurities.
  • Mg in the plating layer is an element that improves the corrosion resistance of the coated steel, and as a result, corrosion resistance is improved because corrosion products are uniformly generated and the corrosion products formed through this do not proceed further corrosion.
  • Mg when added in an amount of less than 1.0%, the effect of improving corrosion resistance is insignificant.
  • Mg exceeds 2.0%, floating dross in the plating bath due to Mg oxidation in the plating bath increases, and dross removal is frequently performed. The problem arises that the operability deteriorates because For this reason, in the prior art, in the case of Zn-Mg-Al-based zinc alloy plating, Mg was added in an amount of 1.0% or more, but the upper limit of the Mg content was set around 3.0%.
  • the Mg content in the plating layer is added to 4.0% or more, and Al may be added to 5.1% or more to suppress Mg oxide dross in the zinc alloy plating bath.
  • Al is combined with Zn and Mg to improve the corrosion resistance of the plated steel sheet.
  • Mg is known to play an auxiliary role in further stabilizing the formation of Zn corrosion products. Since the rate at which Mg is corroded by itself is faster than the rate, and the corrosion resistance of the plated steel sheet may be deteriorated, the upper limit of the Mg content in the plating layer may be limited to 10% or less.
  • the melting point becomes 480° C. or higher.
  • the temperature of the plating bath is set 40 to 60° C higher than the melting point of the plating composition system.
  • the plating bath temperature is too high, erosion of the plating bath structure and deterioration of the steel material may occur.
  • the Al content may be limited to 25% or less.
  • Al and Mg contents may be determined to be located in the 2 eutectic line of MgZn 2 and Al in the Mg-Al-Zn ternary phase diagram.
  • the determination to be positioned in the second process line includes a case in which the position is determined to be precisely positioned in the second process line, as well as a case in which the position is determined to be located in the vicinity of the second process line slightly out of the second process line.
  • the remainder may be Zn and other unavoidable impurities.
  • Inevitable impurities may be unintentionally mixed in the manufacturing process of a conventional hot-dip galvanized steel sheet, and it cannot be completely excluded, and those skilled in the art can easily understand the meaning.
  • spangle tends to appear in hot-dip galvanized steel sheet.
  • These spangles occur due to the properties of the coagulation reaction of zinc. That is, when zinc is solidified, dendrites in the form of branches grow from the solidification nucleus as a starting point to form the skeleton of the plating structure, and the unsolidified molten zinc pool remaining between the dendrites It is finally solidified to complete the solidification of the plating layer. If Al is separated from MgZn 2 and formed into a primary structure, the Al primary structure grows in the form of dendrites, and this Al dendrite form becomes more severe as the plating amount increases or the solidification rate is slow.
  • the Al and Mg contents can be solved by determining to be located in the 2 eutectic line of MgZn 2 and Al in the Mg-Al-Zn ternary phase diagram.
  • the coating layer of Zn-Mg-Al-based in the present invention comprises a Zn-Al-MgZn 2 3 won process organization, Zn-MgZn 2 2 won process organization, Zn is employed the Al least one of the single-phase tissue and Zn single phase tissue has a microstructure that And, since the MgZn 2 structure contains agglomerated Al, it is possible to solve the problem of sequin generation as described above.
  • a Fe-Al-Zn interface alloy layer made of an intermetallic compound of Fe-Al-Zn may be formed between the base steel sheet and the plating layer.
  • the interfacial alloy layer may be formed by Al and Zn in the plating bath and Fe diffused from the base steel sheet in the initial plating stage, and serves to improve the adhesion between the base steel sheet and the plating layer, and at the same time, the Fe from the base steel sheet to the plating layer. It can act as a suppression layer to prevent further diffusion.
  • the interfacial alloy layer has a dendritic shape having a Fe-Al-Zn composition, and this dendritic interfacial alloy phase induces an anchoring effect (anchor effect), which is very advantageous in reducing cracks during bending.
  • the thickness of the Fe-Al-Zn interfacial alloy phase is limited to 0.5 ⁇ m or more and 2 ⁇ m or less. If the thickness is less than 0.5 ⁇ m, the shape of the interfacial alloy phase is not sufficiently grown in a dendritic form, it is not possible to induce an anchoring effect between the base steel sheet and the plating layer, and the bending workability is inferior. On the other hand, if it exceeds 2 ⁇ m, the lower portion of the interfacial alloy phase in the direction of the base steel sheet may grow thickly in the form of a layer, making it vulnerable to interfacial fracture during processing.
  • the hot-dip galvanized steel sheet of the present invention having the configuration as described above, since the plating layer is composed of the alloy composition and microstructure described above, can provide superior corrosion resistance than the conventional zinc-based alloy-coated steel sheet containing Mg within about 3.0%. In addition, the width of cracks during bending can be minimized.
  • the method for manufacturing a hot-dip galvanized steel sheet of the present invention comprises the steps of preparing a base steel sheet; Hot-dip galvanizing the base steel sheet in a plating bath containing, by weight, Al: 5.1 to 25%, Mg: 4.0 to 10%, the remaining Zn and other unavoidable impurities; and cooling the plated steel sheet using an inert gas at a cooling rate of 5 to 30° C./s from the plating bath surface to the top roll section to cool the interfacial alloy layer and Zn-Mg on the base steel sheet.
  • the present invention is not limited to the specific type of the steel plate.
  • a cold-rolled steel sheet or a hot-rolled steel sheet which is a general carbon steel, can be used without limitation.
  • the base steel sheet is immersed in a plating bath containing, by weight, Al: 5.1 to 25%, Mg: 4.0 to 10%, the remaining Zn and other unavoidable impurities, and hot-dip galvanizing.
  • the plating bath of the present invention does not contain Si, by weight, Al: 5.1 to 25%, Mg: 4.0 to 10%, the remaining Zn and other unavoidable impurities are prepared by preparing a plating bath.
  • a plating bath having the above composition a composite ingot containing predetermined Zn, Al, or Mg or a Zn-Mg, Zn-Al ingot containing individual components may be used.
  • Al and Mg contents in the plating bath may be determined to be located in the 2 process line of MgZn 2 and Al in the Mg-Al-Zn ternary phase diagram.
  • hot-dip plating is performed by immersing the base steel sheet in a plating bath having the above composition.
  • the temperature of the plating bath is determined in consideration of the thickness of the interfacial alloy layer constituting the finally manufactured plated steel sheet.
  • the plating is performed by immersion in a plating bath having a temperature (T) such that the thickness (H) of the interfacial alloy layer defined by the following relation 1 can satisfy the range of 0.5 to 2 ⁇ m.
  • T temperature
  • the morphology of the interfacial alloy layer of the Fe-Al-Zn composition constituting the hot-dip galvanized steel sheet to be manufactured can be prepared in a dendritic form.
  • the interfacial alloy phase of such a dendritic form induces an anchoring effect (anchor effect), which is very advantageous in reducing cracks during bending.
  • the plating bath temperature is too low, the dissolution of the ingot is very slow, and it may be difficult to secure excellent plating layer surface quality because the plating bath has high viscosity.
  • it is too high there may be a problem that ash defects caused by Zn evaporation are induced on the plating surface.
  • an excessively high plating bath temperature when Si is not added may induce excessive Fe elution from the base steel sheet to the plating layer, thereby causing outburst, which is the cause of peeling of the plating layer.
  • the temperature (T) of the plating bath should be set to a condition in the range of 470 to 520 °C, and the interfacial alloy phase
  • the relation with the thickness (H) satisfies the above relation (1).
  • the temperature of the base steel sheet during immersion in the plating bath preferably has a range of 5°C or more and not more than 10°C than the temperature of the plating bath, and it is desirable to immerse in the plating bath with a bathing time of 1 to 5 seconds.
  • the interfacial alloy layer on the base steel sheet by cooling the plated steel sheet using an inert gas at a cooling rate of 5 to 30° C./s from the plating bath surface to the top roll section.
  • a hot-dip galvanized steel sheet in which a Zn-Mg-Al-based plating layer is sequentially formed is prepared.
  • the plated steel sheet is pulled up and cooling is started from the hot water surface, and cooling is performed using an inert gas at a rate of 5 ⁇ 30°C/s to the top roll section.
  • the inert gas may be one of N, Ar, and He, and it is more preferable to use N in terms of reducing manufacturing cost.
  • the cooling rate between the hot water surface and the top roll section is 5° C./sec or less, the MgZn 2 structure develops too coarsely, and the surface curvature of the plating layer may be severe.
  • the Zn-MgZn 2 binary process structure is widely formed, it may be disadvantageous in securing uniform corrosion resistance and workability.
  • the cooling rate exceeds 30 ° C / s, solidification starts from the liquid phase to the solid phase during the hot dip plating process, and rapid solidification occurs in the solid-liquid section of 60 to 100 ° C, the temperature range during which all the liquid phases change to the solid phase, The alloy structure may not be uniformly formed, which may result in non-uniform local corrosion resistance.
  • the diffusion of the Fe-Al-Zn phase is insufficient, so that the interfacial alloy phase cannot grow in a dendritic form and is excessively suppressed, which may deteriorate the workability.
  • the amount of nitrogen used may increase for an excessive cooling rate, thereby increasing the manufacturing cost.
  • a cold-rolled steel sheet containing C: 0.018%, Mn: 0.2%, Si: 0.001%, P: 0.009%, Al: 0.022%, and the balance consisting of Fe and unavoidable impurities was prepared. Thereafter, hot-dip galvanizing was performed so that the plating adhesion amount on one side of the cold-rolled steel sheet was 140 g/m 2 , and then cooled at a rate of 15° C./s from the molten metal surface to the top-roll to obtain a Zn-Mg-Al-based alloy plated steel sheet. .
  • the composition of the plating solution was changed to 2.8 to 13% Al and 2.2 to 5.1% Mg by weight%. Except for the components that are inevitably present in the plating bath, the rest is Zn.
  • Component analysis of the plating layer was carried out by wet analysis of the solution after the plating layer was completely dissolved by immersion in 5% hydrochloric acid, and the results are shown in Table 1. For reference, in Table 1 below, Fe among the components of the plating layer is diffused from the base steel sheet during hot-dip galvanizing.
  • the steel sheets having the plating layer composition of Table 1 were immersed in the plating bath temperature of Table 2 to prepare a plated steel sheet.
  • the thickness of the interfacial alloy layer of the final prepared hot-dip galvanized steel sheet was measured and shown in Table 2 below.
  • the target interfacial alloy layer thickness calculated according to the plating bath temperature by relation 1 is also shown in Table 2 below.
  • Inventive Example 1-2 is a case where plating is performed under conditions that satisfy both the plating component system and the plating bath temperature range proposed in the present invention.
  • the Mg content was less than 4.0%, which is the range suggested by the present invention, and Si was added, and Comparative Example 3 was prepared using a plating bath containing both Mg and Al content. represents one case.
  • Comparative Example 4-6 satisfies the plating Al, Mg component system proposed in the present invention, but unlike Inventive Example 1-2, the plating bath temperature range was high at 530 ° C. or higher, so that the alloying between the plating layer and the base steel sheet was excessive. Occurs, indicating a case in which the Fe component is contained at a level of 7.1 to 8.7% in the plating layer.
  • Table 2 shows the calculated thickness of the interfacial alloy layer calculated by Relation 1 and the average thickness of the final interfacial alloy layer according to the plating bath temperature.
  • Inventive Example 1-2 satisfies the plating bath temperature range of 470 to 520° C. proposed in the present invention, and it can be confirmed that the thickness of the interfacial alloy layer calculated by Relation 1 and the thickness of the final interfacial alloy layer are similar.
  • Comparative Example 1-3 is a case outside the plating component system limited in the present invention, and in Comparative Example 1-2, the component system containing Si, which is a component that suppresses alloying between the base steel sheet and the plating layer, is the thickness of the interfacial alloy layer.
  • the plating bath temperature is 530° C., 540° C., and 570° C., respectively, and is out of the plating bath temperature range applicable to Relational Equation 1.
  • FIG. 1 the cross section of the hot-dip galvanized steel sheet of Inventive Example 1, which is a preferred embodiment of the present invention, is observed with a Field Emission Scanning Electron Microscope (hereinafter referred to as 'FE-SEM') (magnification ⁇ 2000 times) represents a picture.
  • FIG. 2 is a photograph of the surface of the interfacial alloy layer of the hot-dip galvanized steel sheet of Invention Example 1, which is a preferred embodiment of the present invention, observed by FE-SEM (magnification ⁇ 10,000 times).
  • the coating layer of the invention example 1 Zn-Al-MgZn 2 3 ternary process organization and Zn-MgZn 2 2 contained a ternary process organization and, Zn employment Al phase tissue, Zn single phase organization and MgZn 2 It can be confirmed that the organization is included. In addition, it can be seen that the Al structure darkly expressed is located in the MgZn 2 structure. In addition, it can be confirmed that the interfacial alloy layer made of Fe-Al-Zn is formed in a dendritic form with a thickness of 0.5 ⁇ m or more and 2 ⁇ m or less, as shown in FIG. 2 .
  • FIG. 3 is a mapping of Fe, Al, and Zn components observed by TEM-EDS of a replica sample obtained from cross-sectional polishing of the interfacial alloy layer of the hot-dip galvanized steel sheet of Invention Example 1, which is a preferred embodiment of the present invention.
  • ) is a picture.
  • 4 is a weight percentage (wt%) detected along the yellow line shown in FIG. 3 for the interfacial alloy layer of the hot-dip galvanized steel sheet of Invention Example 1, which is a preferred embodiment of the present invention.
  • Si is not contained in the components of the interfacial alloy layer, Fe: 20-35 wt%, Al: 15-30 wt%, Zn: alloy in the composition range of 30-36 wt% It can be seen that the phase is formed.
  • Each plated steel sheet was loaded into a salt spray tester, and the appropriate generation time was measured according to the international standard (ASTM B117-11). At this time, 5% brine (temperature 35 °C, pH 6.8) was used, and 2ml/80cm 2 brine was sprayed per hour. And in order to exclude the influence of the difference in the amount of plating, the time elapsed (hr) until the occurrence of red rust was divided by the amount of plating (g/m 2 ) and expressed as a corrosion resistance index for evaluation.
  • the length of the top of the bending is 1mm by SEM. After observation, the width of the bending crack was observed and evaluated by averaging.
  • the width of the bending crack exceeds 60 ⁇ m and 100 ⁇ m or less
  • the excellent bending properties of Inventive Example 1-2 are considered to be due to the fact that the interfacial alloy phase in the dendritic form induces an anchoring effect (anchor effect), thereby advantageously reducing cracks during bending.
  • the composition of the plating bath is within the range of the present invention, but in Comparative Examples 4-6 where the plating bath temperature is outside the range of the present invention, the interfacial alloy layer is not in the dendritic form proposed in the present invention, and alloying proceeds throughout the plating layer. As a result, it can be confirmed that the width of the bending crack exceeds 100 ⁇ m, and the bending workability is very poor.
  • FIG. 6 is a photograph of the hot-dip galvanized steel sheet of Comparative Example 1, after bending at 90 degrees, the cracks generated at the top of the bending were observed with FE-SEM (magnification ⁇ 100, ⁇ 200, ⁇ 300 times).
  • FIG. 7 is a photograph obtained by observing the cross section of Comparative Example 4 by FE-SEM (magnification ⁇ 2,000 times).
  • Figure 8 is a photograph of the cross section of Comparative Example 5 observed by FE-SEM (magnification ⁇ 2,000 times)
  • Figure 9 is a photograph of the cross section of Comparative Example 6 observed by FE-SEM (magnification ⁇ 2,000 times).

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PCT/KR2020/017344 2019-12-06 2020-12-01 굽힘 가공성 및 내식성이 우수한 용융아연도금강판 및 이의 제조방법 WO2021112519A1 (ko)

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US17/782,401 US20230019786A1 (en) 2019-12-06 2020-12-01 Hot-dipped galvanized steel sheet having excellent bending workability and corrosion resistance and manufacturing method therefor
JP2022532730A JP2023504496A (ja) 2019-12-06 2020-12-01 曲げ加工性及び耐食性に優れた溶融亜鉛めっき鋼板及びその製造方法
CN202080084257.3A CN114787411B (zh) 2019-12-06 2020-12-01 弯曲加工性和耐蚀性优异的热浸镀锌钢板及其制造方法
EP20897267.9A EP4071265A4 (en) 2019-12-06 2020-12-01 HOT-DIP GALVANIZED STEEL SHEET EXHIBITING EXCELLENT BENDABILITY AND CORROSION RESISTANCE PROPERTIES AND METHOD OF MANUFACTURING THEREOF

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